WO2011151908A1 - Tube d'acier pour coussin de sécurité gonflable et son processus de fabrication - Google Patents

Tube d'acier pour coussin de sécurité gonflable et son processus de fabrication Download PDF

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WO2011151908A1
WO2011151908A1 PCT/JP2010/059417 JP2010059417W WO2011151908A1 WO 2011151908 A1 WO2011151908 A1 WO 2011151908A1 JP 2010059417 W JP2010059417 W JP 2010059417W WO 2011151908 A1 WO2011151908 A1 WO 2011151908A1
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Prior art keywords
steel pipe
content
steel
toughness
mass
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PCT/JP2010/059417
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English (en)
Japanese (ja)
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勇次 荒井
高野　孝司
卓磨 川本
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住友金属工業株式会社
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Priority to EP10852513.0A priority Critical patent/EP2484793B1/fr
Priority to CA2776984A priority patent/CA2776984C/fr
Priority to KR1020127010714A priority patent/KR101425738B1/ko
Priority to MX2012005710A priority patent/MX2012005710A/es
Priority to ES10852513T priority patent/ES2726767T3/es
Priority to PCT/JP2010/059417 priority patent/WO2011151908A1/fr
Priority to IN3019DEN2012 priority patent/IN2012DN03019A/en
Priority to CN201080049152.0A priority patent/CN102741438B/zh
Priority to PL10852513T priority patent/PL2484793T3/pl
Publication of WO2011151908A1 publication Critical patent/WO2011151908A1/fr
Priority to US13/438,956 priority patent/US9080223B2/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/10—Modifying the physical properties of iron or steel by deformation by cold working of the whole cross-section, e.g. of concrete reinforcing bars
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60R—VEHICLES, VEHICLE FITTINGS, OR VEHICLE PARTS, NOT OTHERWISE PROVIDED FOR
    • B60R21/00—Arrangements or fittings on vehicles for protecting or preventing injuries to occupants or pedestrians in case of accidents or other traffic risks
    • B60R21/02—Occupant safety arrangements or fittings, e.g. crash pads
    • B60R21/16—Inflatable occupant restraints or confinements designed to inflate upon impact or impending impact, e.g. air bags
    • B60R21/26—Inflatable occupant restraints or confinements designed to inflate upon impact or impending impact, e.g. air bags characterised by the inflation fluid source or means to control inflation fluid flow
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C21D9/085—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/32—Soft annealing, e.g. spheroidising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C21D1/42—Induction heating
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the present invention relates to a steel pipe for an airbag having a high strength of a tensile strength of 1000 MPa or more and a high toughness of vTrs100 of ⁇ 80 ° C. or less, and a method for producing the same. More specifically, the present invention can be manufactured by a relatively inexpensive and simple manufacturing process, and can be applied with a short-time quenching heat treatment using rapid heating means such as high-frequency induction heating. It is related with a steel pipe and its manufacturing method.
  • an airbag system has been developed and mounted. This is a system that reduces the injury by absorbing the kinetic energy of the occupant by deploying an air bag with gas or the like between the occupant and the occupant before the occupant collides with the steering wheel or the instrument panel in the event of a vehicle collision. It is. Conventionally, a system using explosive chemicals has been adopted as an air bag system. However, in recent years, a system using a high-pressure filling gas has been developed and its application is spreading.
  • the above-mentioned system using high-pressure filling gas is to keep the gas etc. constantly at a high pressure and to inject the high-pressure gas into the air bag at the time of collision. Therefore, the steel pipe used for the accumulator of high-pressure gas is extremely Stress is applied at a large strain rate in a short time. For this reason, the steel pipe is required to have high dimensional accuracy, workability and weldability, unlike a simple structure such as a conventional pressure cylinder or line pipe, and also requires high strength and excellent burst resistance. Is done.
  • an ultra-high-strength seamless steel pipe having a tensile strength exceeding 1000 MPa has been used as an accumulator in an airbag system.
  • the burst pressure is about 100 MPa at a TS of 800 MPa, whereas the burst pressure increases to 130 MPa when the TS is 1000 MPa.
  • the thickness can be reduced by about 20%.
  • the accumulator needs to have excellent low temperature toughness so that the accumulator is not brittlely broken and causes a secondary disaster at the time of collision.
  • a seamless steel pipe for an accumulator has been given high strength and high toughness by quenching and tempering.
  • the accumulator is required to have sufficient low temperature toughness even in a temperature range of ⁇ 60 ° C. or lower in a state after undergoing diameter reduction processing as described later.
  • an accumulator for an air bag is cut into a predetermined length by cutting a seamless steel pipe, which is a raw pipe, into a short pipe, and at least one end thereof is reduced in diameter by pressing or spatula drawing (this) Is called bottle processing), and finally processed into a shape necessary for mounting an initiator or the like. Therefore, in order to guarantee the operation as an accumulator for an air bag, there are cases in which only the toughness of the seamless steel pipe as a material is incomplete. This is because the toughness of the bottle portion is reduced by the diameter reduction processing, which is the final processing, and cracks may occur during high-pressure loading. Therefore, in consideration of such a decrease in toughness, the seamless steel pipe used for the airbag accumulator needs to have toughness lower than the operating environment temperature of the accumulator.
  • the jointed steel pipe constituting the accumulator has an elongation of 10% or more, a tensile strength of 1000 MPa or more, and has a ductile fracture surface in a Charpy impact test at ⁇ 80 ° C., preferably ⁇ 100 ° C.
  • Low temperature toughness that is, low temperature toughness where vTrs100 is ⁇ 80 ° C. or lower, preferably ⁇ 100 ° C. or lower) is required.
  • Patent Document 1 discloses a conventional technique related to a seamless steel pipe for an airbag system having a high strength and high toughness with a tensile strength of 1000 MPa or more.
  • Patent Document 1 after making a seamless steel pipe by using a steel material having a chemical composition in a predetermined range, the seamless steel pipe is subjected to cold drawing to obtain a steel pipe having a predetermined dimension, and the Ac3 transformation point.
  • a method for producing a seamless steel pipe for an air bag is proposed in which the steel is heated to a temperature in the range of 1050 ° C. or less, then quenched, and then tempered at a temperature in the range of 450 ° C. or more and the Ac1 transformation point or less. .
  • this method it is excellent in workability and weldability at the time of manufacturing an inflator for an airbag. Further, as an inflator, it has a tensile strength of 900 MPa or more and a high ductility in a drop test at ⁇ 60 ° C. against a halved steel pipe. It is said that a seamless steel pipe having toughness can be obtained. However, this method is expensive because it needs to contain a large amount of Cr as a steel composition in order to obtain strength and toughness.
  • Patent Document 2 shows that when high-frequency heating and quenching is employed, a high-strength and high-toughness seamless steel pipe for an airbag system having a tensile strength exceeding 1000 MPa can be produced by fine graining by rapid heating.
  • a steel material having a chemical composition in a predetermined range is formed into a seamless steel pipe, and then the seamless steel pipe is subjected to a cold drawing process to obtain a steel pipe having a predetermined size, and 10 ° C./second.
  • a cold drawing process After heating to 900 to 1000 ° C. at the above heating rate, quenching is performed, and then tempering is performed at a temperature not higher than the Ac1 transformation point. It is intended to obtain a high toughness that exhibits ductility even in a burst test at ⁇ 80 ° C. or lower.
  • Patent Document 2 a specific example in which heating for quenching is performed at 20 ° C./second is shown.
  • Patent Document 3 also shows an example of using induction heating and quenching, but as shown in Table 3 of Examples of the same document, only short-time heating in the range of 900 to 1000 ° C. is assumed. There are similar problems.
  • Patent Document 4 induction heating and quenching is used, but as shown in the examples, this is a result of heating in the range of 920 to 940 ° C. and has the same problem as Patent Document 2.
  • this burst resistance performance has a 100% ductile fracture lower limit temperature (vTrs100) in a Charpy impact test of ⁇ 80 ° C. or lower, preferably ⁇ 100 ° C. or lower.
  • Patent Document 1 since a large amount of Cr is contained, cold drawing workability is not sufficient, and a large degree of workability is ensured at the cold drawing stage. For this purpose, there are problems that intermediate softening annealing is required in the middle and the manufacturing cost increases. In addition, exhibiting ductility in a drop weight test at ⁇ 60 ° C. does not necessarily mean exhibiting ductility in a burst test at ⁇ 60 ° C.
  • the manufacturing process is simple.
  • most steel compositions have a sum of Cr and Mo contents in the range of more than 0.6%.
  • the strength of the seamless steel pipe is increased after hot pipe forming, and the cold drawing process becomes difficult due to the increased strength.
  • Softening annealing is required before processing, which complicates the process and increases costs.
  • the present invention is suitable for quenching by low-frequency mass-production high-frequency induction heating, which has the performance required today as an accumulator for airbags, that is, sufficient performance for increasing accumulator pressure and thinning of steel pipes.
  • An object of the present invention is to provide a high steel pipe for an air bag and a method for manufacturing the same.
  • the final product has a tensile strength of 1000 MPa or more, preferably 1050 MPa or more, and is excellent in low-temperature toughness that exhibits ductile fracture even in a burst test at ⁇ 60 ° C., particularly 100% ductile fracture lower limit temperature
  • the steel pipe described in the above (I) is designed to be an alloy that can be manufactured in a state where stable characteristics can be obtained even by quenching heat treatment by mass-production high-frequency heating, and more specifically Specifically, there is a need for a method of manufacturing a steel pipe for an air bag that can be provided as a tough product having a certain level or higher even when the heating temperature for heating and quenching exceeds 1000 ° C. (eg, 1020 to 1040 ° C.). It is called Technical Issue (IV).
  • the present inventors investigated the relationship among alloy elements, strength and low temperature toughness in a seamless steel pipe for an airbag system that is quenched and tempered after cold working.
  • the outstanding balance of strength and toughness required today includes Mn at a low level, even if Mo is not contained, and has been added in large quantities so far. It was found that the steel was obtained by adding a small amount of Cr, which had been used, and steel containing appropriate amounts of Cu, Ni, Ti, and B.
  • the present inventors examined the influence of alloying elements on the strength and toughness of a seamless steel pipe for an airbag system manufactured by quenching and tempering after cold working and having a TS exceeding 1000 MPa. As a result, the following knowledge was obtained and the present invention was completed.
  • the present invention has been completed based on the above findings and further studies.
  • the gist of the present invention is as follows. (1) C: 0.05 to 0.20%, Si: 0.10 to 0.50%, Mn: 0.10 to 1.00%, P: 0.025% or less, S: 0.005%
  • the steel pipe for an air bag according to (1) characterized in that the Ti content is in mass% and has a steel composition of more than 0.020% and not more than 0.050%.
  • Mo represents (Cr + Mo), and the element symbol means a numerical value when the content of these elements is expressed in mass%. When the Mo content is 0, 0 (zero) is substituted for Mo in the formula (1).
  • the seamless steel pipe for an airbag system according to any one of (1) to (3), further having a steel composition containing V: 0.02 to 0.20% (5)
  • a seamless steel pipe made by hot pipe making using a billet having the steel composition described in any one of 1) to (4) is cooled to a cold working degree of 40% or more.
  • a steel pipe of a predetermined size is formed by performing inter-working, and after correction, if necessary, quenching is performed by heating to a temperature not lower than the Ac3 transformation point by high-frequency heating and quenching, and then heating to a temperature not higher than the Ac1 transformation point.
  • a method for producing a seamless steel pipe for an air bag characterized by performing tempering.
  • a seamless steel pipe having extremely high strength and excellent low-temperature burst performance can be provided, and the pressure of an air bag accumulator whose diameter is reduced at the end (pressure of 145 MPa or more) / thin wall weight reduction ( (Example: Seamless steel pipe having a wall thickness of 3.6 mm to 1.7 mm and a diameter of 60.3 mm to 25.0 mm).
  • FIG. 1 is a graph showing the relationship between Cr + Mo and Cu + Ni in a preferred embodiment of the present invention. It is explanatory drawing of the test piece used for the characteristic evaluation in the Example of this invention.
  • C 0.05-0.20% C is an element effective for increasing the strength of steel at low cost, but if its content is less than 0.05%, it is difficult to obtain a desired tensile strength of 1000 MPa or more, and if it exceeds 0.20%, it is processed. And weldability are reduced. Therefore, the C content is set to 0.05 to 0.20%. A preferred range for the C content is 0.07 to 0.17%.
  • Si 0.10 to 0.50%
  • Si is an element that improves the hardenability of the steel and improves the strength, and a content of 0.10% or more is necessary.
  • the Si content is set to 0.10 to 0.50%.
  • a preferable range of the Si content is 0.20 to 0.50%.
  • Mn 0.10 to 1.00%
  • Mn has a deoxidizing action and is an effective element for improving the hardenability of steel and improving the strength and toughness. However, if its content is less than 0.10%, sufficient strength and toughness cannot be obtained. On the other hand, if it exceeds 1.00%, MnS coarsens, which is stretched during hot rolling, and toughness. Decreases. In the present invention, even if Mn is suppressed to 1.00% or less, it is necessary to ensure the intended tensile strength of 1000 MPa or more and excellent low-temperature burst performance. In order to improve the hardenability. Therefore, the Mn content is set to 0.10 to 1.00%. The Mn content is preferably 0.40 to 0.90% from the viewpoint of balance between strength and toughness.
  • P 0.025% or less P causes a decrease in toughness due to grain boundary segregation. In particular, when the content exceeds 0.025%, the decrease in toughness becomes significant. Therefore, the content of P is set to 0.025% or less.
  • the P content is preferably 0.020% or less, and more preferably 0.015% or less.
  • S decreases the toughness particularly in the steel pipe T direction, that is, in the direction orthogonal to the rolling direction (longitudinal direction) of the steel pipe.
  • the content of S is set to 0.005% or less.
  • the S content is preferably 0.003% or less.
  • Al 0.005% or more and 0.10% or less
  • Al is an element having a deoxidizing action and effective in improving toughness and workability. However, if the content exceeds 0.10%, the generation of ground becomes remarkable. Therefore, the Al content is set to 0.10% or less. In addition, in order to acquire such an effect of Al, it is necessary to make it contain 0.005% or more.
  • the Al content in the present invention refers to the content of acid-soluble Al (so-called “sol.Al”).
  • Ca 0.0005 to 0.0050%
  • Ca has an effect of fixing S present as an inevitable impurity in the steel as a sulfide, improving anisotropy of toughness, and increasing the T-direction toughness of the steel pipe, thereby increasing the burst resistance. This effect is manifested at a content of 0.0003% or more, particularly 0.0005% or more. However, if the content exceeds 0.0050%, inclusions increase and the toughness decreases. Therefore, the Ca content is set to 0.0005 to 0.0050%.
  • Nb 0.005 to 0.050%
  • Nb is finely dispersed as carbide in the steel and has an effect of strongly pinning the crystal grain boundary. Thereby, it has the effect of making the crystal grains finer and improving the toughness of the steel. In order to acquire the effect, it contains 0.005% or more, but if it contains more than 0.050%, the carbide is coarsened and the toughness is lowered. Therefore, the Nb content is set to 0.005 to 0.050%.
  • Ti 0.005 to 0.050%
  • Ti has the effect of fixing N in steel and improving toughness.
  • the finely dispersed Ti nitride has the effect of strongly pinning the crystal grain boundaries, making the crystal grains finer, and improving the toughness of the steel.
  • fixing N in steel is also important for bringing out the effect of B described later. Therefore, in order to obtain these effects, 0.005% or more is contained, but if it exceeds 0.050%, the nitride is coarsened and the toughness is lowered. Therefore, the Ti content is set to 0.005 to 0.050%.
  • the preferable content is more than 0.020% to 0.035%.
  • B 0.0005 to 0.0050% B segregates at the grain boundaries in the steel, remarkably improves the hardenability of the steel, and contributes to improved toughness.
  • the effect is expressed by containing 0.0005% or more.
  • the B content is set to 0.0005 to 0.0050%. Preferably, it is 0.0030% or less.
  • blending B improves strength by improving hardenability. If B is not in a solid solution state, it does not segregate at the grain boundaries. Therefore, it is preferable that N which can easily form a compound with B is fixed by Ti, and B is preferably contained in an amount more than the amount fixed by N. In that sense, the B content preferably satisfies the relationship of the following formula (2) or (3) from the stoichiometric ratio of B, Ti, and N.
  • N-Ti / 3.4 ⁇ 0 B ⁇ 0.0005 When N-Ti / 3.4> 0, B- (N-Ti / 3.4) ⁇ (10.8 / 14) ⁇ 0.0005 (3)
  • B, N, and Ti in the formula (2) are numerical values when the content of each element is expressed in mass%.
  • the upper limit of the N content is set to 0.010% or less.
  • a preferable range of the N content is 0.002 to 0.008%.
  • Cu 0.01 to 0.50% Cu has the effect of increasing the hardenability of the steel and improving the strength and toughness. The effect is manifested when the content is 0.01% or more, preferably 0.03% or more. However, the content exceeding 0.50% causes a significant increase in alloy cost. Therefore, the Cu content is set to 0.01 to 0.50%.
  • the preferable content is 0.03% or more, particularly 0.05% or more, and more preferably 0.15% or more.
  • Ni 0.01 to 0.50% Ni has the effect of increasing the hardenability of steel and thus improving strength and toughness. The effect is manifested when the content is 0.01% or more, preferably 0.03% or more. However, if the content exceeds 0.50%, the alloy cost will be exceeded. Therefore, the Ni content is set to 0.01 to 0.50%.
  • the preferable content is 0.03% or more, particularly 0.05% or more, and more preferably 0.15% or more.
  • Cr 0.01 to 0.50% Cr has the effect of increasing the hardenability of steel and increasing the resistance to temper softening and improving the strength and toughness. The effect is manifested if each element contains 0.01% or more. However, the content exceeding 0.50% is unsuitable because it causes excessive strength during cold drawing and deteriorates workability. Therefore, the Cr content is set to 0.01 to 0.50%. Preferably, the content is 0.18 to 0.40%.
  • the containing balance is limited as follows. Limited by the formula of Cu, Ni, Cr, Mo content: When Mo is added in the present invention, it is preferable to satisfy the following relationship among the contents of Cu, Ni, Cr, and Mo.
  • Cr and Mo prevent spheroidization of cementite that precipitates during tempering, and in steels containing B as in the present invention, it is easy to form a compound of B (boride) at grain boundaries, High strength materials tend to reduce toughness. Therefore, higher strength by inclusion of Cu and Ni is more targeted by the present invention than higher strength by Cr content (even when Mo is added, limiting Mo to a very small amount). And it is suitable as a high toughness airbag steel pipe. Specifically, it is important to satisfy the following formula (1) for the balance of Cr, Mo, Cu, and Ni.
  • M in the formula (1) represents “Cr + Mo”, and the element symbol is a numerical value when the content of each element is expressed in mass%. When Mo is not contained, 0 is substituted for Mo of “Cr + Mo”.
  • Mo Less than 0.10%
  • Mo is not contained in principle, but a very small amount may be contained if desired.
  • Mo has the effect of improving the hardenability of steel and increasing the resistance to temper softening and improving the strength and toughness. The effect can be observed even in a trace amount, but in order to obtain a certain effect, it is preferable to contain 0.01% or more. However, if 0.10% or more is contained, the alloy cost is exceeded.
  • Mo content is high, the strength tends to be high even in the air cooling after the hot pipe making of the seamless steel pipe, and a softening heat treatment is required before the cold drawing process, resulting in an increase in manufacturing cost. Therefore, even when Mo is added, the Mo content is less than 0.10%.
  • V 0.02 to 0.20%
  • V has an effect of increasing strength by precipitation strengthening.
  • the content of V is 0.02% or more, the effect is exhibited, but when it exceeds 0.20%, the toughness is lowered. Therefore, when V is added, the content of V is preferably 0.02 to 0.20%.
  • a preferable range of the V content is 0.03 to 0.10%.
  • a cast piece cast by a continuous casting machine having a cylindrical mold may be used, or a cast piece cast into a rectangular mold and then formed into a cylindrical shape by hot forging.
  • the steel according to the present invention suppresses the addition of ferrite stabilizing elements such as Cr (when adding Mo, Cr and Mo) and adds austenite stabilizing elements such as Cu and Ni. Even when continuous casting is performed in a round shape, the effect of preventing center cracking is great, and it can be used as a round CC billet.
  • the steel composition of the present invention is suitable for a seamless steel pipe for an airbag accumulator.
  • a steel pipe may be manufactured using the slab described in (B) whose chemical composition is adjusted as described above as a raw material, and the pipe making method of the steel pipe is particularly limited. is not. For example, the Mannesmann-Mandrel method is adopted.
  • the steel pipe produced as a seamless steel pipe as described above is cold worked under conditions that provide predetermined dimensional accuracy and surface properties.
  • the cold working only needs to obtain predetermined dimensional accuracy and surface properties.
  • the cold working is not particularly limited to specific methods such as cold drawing and cold rolling.
  • the degree of processing is preferably 3% or more in terms of area reduction (section reduction rate).
  • it exceeds 50% the development of wrinkles on the inner surface is generally remarkable, so it should be less than 50%. preferable.
  • cold working is performed multiple times to obtain the final product dimensions.
  • the thickness that is, as the degree of work increases, the strength of the steel pipe increases due to work hardening.
  • the steel according to the present invention can achieve a degree of work reduction of 40% or more, preferably over 40%, without performing preheating softening treatment or intermediate softening annealing even during cold working.
  • the area reduction rate is synonymous with the cross-section reduction rate and is defined by the following equation.
  • Area reduction ratio (%) (S 0 ⁇ S f ) ⁇ 100 / S 0
  • S 0 Cross-sectional area of the steel pipe before cold working
  • S f Cross-sectional area of the steel pipe after completion of cold working
  • the total area reduction rate is also treated as the above area reduction rate.
  • the present invention does not exclude cold working in which soft annealing is performed in the middle.
  • cold processing eg, cold drawing
  • This straightening process is not particularly limited, but, for example, two roll-type rolling mills are provided in about four rows, the center positions of the roll gaps in each row are staggered (that is, offset), and the roll gap is further increased.
  • a method of adjusting and bending and unbending by passing a steel pipe between them is preferable.
  • the offset amount is 1% or more of the outer diameter of the steel pipe and the roll gap amount is 1% or less of the outer diameter of the steel pipe.
  • the offset amount is 50% or less of the outer diameter of the steel pipe and the roll gap amount is 5% or more of the outer diameter of the steel pipe, there is no problem such as generation of wrinkles on the inner surface of the steel pipe.
  • the heating rate at this time can be adjusted with the feed rate of the steel pipe which passes along a high frequency coil etc., it is preferable to set it as about 25 degreeC / second or more. More preferably, it is 50 degreeC / second or more, More preferably, it is 100 degreeC / second or more.
  • the cooling after heating to a temperature of at least the Ac3 transformation point is rapid cooling in order to obtain a desired tensile strength of 1000 MPa or more stably and reliably, but it is preferable to perform a rapid cooling treatment such as water quenching.
  • a rapid cooling treatment such as water quenching.
  • the cooling rate between 800 ° C. and 500 ° C. during the rapid cooling treatment is preferably 50 ° C./second or more. More preferably, it is 125 ° C./second or more.
  • the steel pipe that has been quenched and cooled to near normal temperature is tempered at a temperature not higher than the Ac1 transformation point in order to impart desired tensile strength of 1000 MPa or more and burst resistance.
  • the bending may be corrected with a straightener or the like as appropriate by the method described in (E). Even if the steel pipe having the steel composition described in (A) is used, the strength and toughness intended by the present invention cannot be stably secured if the heating rate in the quenching stage or the cooling rate is insufficient. There is a case.
  • the seamless steel pipe tempered in this way is cut into a predetermined length by cutting it into a predetermined length, and at least one end thereof is reduced in diameter by press working or spatula drawing, etc. It is finally processed into a shape necessary for mounting, and used as an airbag accumulator.
  • Example 1 This example was conducted in order to investigate the relationship between the steel composition and the low temperature toughness of a material manufactured by simulating the manufacturing conditions of a seamless steel pipe.
  • Steels having the chemical compositions of the six steel types shown in Table 1 were melted by vacuum melting and cold-rolled after hot rolling to obtain 5 mm-thick plate (working degree: 40%). Then, it heated to 920 degreeC with the average temperature increase rate of 300 degrees C / sec by high frequency heating, and after holding
  • Table 2 shows the tensile strength (TS) of each steel obtained by the tensile test and the 100% ductile fracture surface lower limit temperature (vTrs100) obtained by the Charpy impact test.
  • TS tensile strength
  • vTrs100 100% ductile fracture surface lower limit temperature
  • FIG. 1 the total Cr and Mo contents and the total Cu and Ni contents of each steel of this example are plotted, and vTrs100 is ⁇ 80 ° C. or higher, ⁇ , and ⁇ 100 ° C. or higher. Is indicated by a circle. From FIG. 1, it is understood that excellent low temperature toughness can be ensured by satisfying the relationship of the formula (1) with respect to the total content of Cr and Mo with respect to the total content of Cu and Ni.
  • Example 2 Steel having the chemical composition shown in Table 3 was melted in a converter, and a cylindrical billet having an outer diameter of 191 mm was manufactured by continuous casting.
  • the round CC billet was cut to a desired length, heated to 1250 ° C., and finished to a diameter of 70 mm and a wall thickness of 4.0 mm by piercing and rolling by a normal Mannesmann-mandrel mill method.
  • the obtained seamless steel pipe was subjected to cold drawing (cold drawing) by an ordinary method as a raw pipe to finish the outer diameter to 60.3 mm and the wall thickness to 3.6 mm. This is steel pipe size 1. After correcting these cold drawn steel pipes with a straightener, they were heated to 920 ° C.
  • the straightening by this steel pipe size 1 straightener is provided with 3 rows of 2 roll type rolling mills, and the center position of the roll gap of the 2nd row is shifted 20 mm above the center position of the 1st row, Further, the center position of the roll gap in the third row is shifted 3 mm above the center position in the first row, and the roll gaps in the second row and the third row are each 58.8 mm (outer diameter -1.5 mm). ) And 57.3 mm (outer diameter -3.0 mm), and bending and unbending were performed by passing a steel pipe between them.
  • a seamless steel pipe having an outer diameter of 51.0 mm and a wall thickness of 3.0 mm finished by drilling and rolling is cold-drawn (cold drawing) by an ordinary method, and the outer diameter is 40.degree.
  • the thickness was 0 mm and the wall thickness was 2.6 mm.
  • This is steel pipe size 2.
  • the straightening with the steel pipe size 2 straightener is performed in the same manner as in the steel pipe size 1, and the center position of the roll gap in the second row is shifted 10 mm above the center position in the first row, and three rows.
  • the center position of the eye roll gap is shifted 3 mm above the center position of the first row, and the roll gaps of the second and third rows are 39.5 mm (outer diameter -0.5 mm) and 39, respectively.
  • the thickness was adjusted to .2 mm (outer diameter -0.8 mm), and bending and unbending were performed by passing a steel pipe between them.
  • a tensile test having the shape shown in FIG. 2 was taken and the strength characteristics were investigated.
  • the numbers in the figure indicate dimensions (unit: mm).
  • six steel pipes subjected to induction hardening and tempering were each cut into 300 mm lengths, and both pipe ends were subjected to press working so that the ratio of the diameter of the reduced diameter portion / the diameter of the unreduced diameter portion was 0.6.
  • a reduced diameter portion having a length of 25 mm was provided to form an accumulator bottle portion. Thereafter, one end was welded and sealed, and the other end was welded with a closing member penetrating the high-pressure hose.
  • This test specimen was immersed in ethanol in a chamber cooled to ⁇ 60 ° C., ethanol was injected into the pipe from a high-pressure hose to increase the internal pressure, and the pipe was ruptured.
  • all six of the steel pipe size 1 and 2 specimens using steel A to steel B have a brittle fracture surface area ratio of less than 5% in the opening and satisfy sufficient burst performance.
  • 3 of each of 6 steel pipe size 1 and 2 specimens using steel C were prematurely broken from the reduced diameter portion, and the burst pressure was significantly reduced.
  • all the six test bodies using the steel D and the steel E had the brittle fracture surface area ratio of the opening part of 5% or more, and did not satisfy performance.
  • Steels A to B in Table 4 are steels whose components satisfy the conditions specified in the present invention.
  • Steels C to E are steels that do not satisfy the relational expression (1) of Cu, Ni, Cr, and Mo contents that are satisfactory in the present invention, or steels that do not satisfy the range of other components.
  • Example 3 Steel having the chemical composition shown in Table 5 was melted in a converter, and a cylindrical billet having an outer diameter of 191 mm was manufactured by continuous casting. This round CC billet was cut to a desired length, heated to 1250 ° C., and then subjected to piercing and rolling by a normal Mannesmann-Mandrel mill method to produce a seamless steel pipe. Thereafter, cold drawing (cold drawing) was performed by a normal method to finish various product steel pipe sizes. Table 6 shows the steel pipe size at the time of hot pipe making and the steel pipe size after the subsequent cold drawing.
  • These cold drawn steel pipes were straightened with a straightener and then heated using a high-frequency induction heating device at an average temperature increase rate of 300 ° C./second under the conditions shown in Table 6, followed by water quenching. .
  • This water quenching was performed by spraying water in a spray form from a nozzle arranged in a ring shape, passing the steel pipe through the ring, and cooling the outer surface of the steel pipe.
  • the high-frequency induction heating apparatus and the water quenching equipment described above are connected, and the cooling speed was changed by changing the passing speed of the steel pipe.
  • a soaking treatment for 30 minutes for tempering was performed in a normal walking beam furnace, and the tensile strength was adjusted to 1000 MPa or more.
  • a fixed length was cut out from each steel pipe subjected to quenching and tempering in this way, and a tensile test was performed in accordance with the metal material tensile test method specified in JISZ 2241 using the collected No. 11 test piece in JISZ 2201. .
  • fixed length was cut out from each steel pipe, it was cut
  • a Charpy impact test was carried out using a test piece in which a 2 mm V notch was introduced into a rectangular material having a length of 55 mm, a height of 10 mm, and a width of the original thickness of the steel pipe taken from the expanded direction from the developed pipe.
  • Table 6 shows the relationship between the lower limit temperature (denoted by vTrs100 in Table 6) at which the ductile fracture surface ratio 100% obtained at this time can be secured and the tensile test results.
  • each of the steel pipes subjected to induction hardening and tempering was cut into 300 mm lengths, and both pipe ends were subjected to press working so that the ratio of the diameter of the reduced diameter portion / the diameter of the unreduced diameter portion was 0.6
  • a reduced diameter portion having a length of 25 mm was provided to obtain the shape of the bottle portion of the accumulator. Thereafter, one end was welded and sealed, and the other end was welded with a closing member penetrating the high-pressure hose.
  • This test specimen was immersed in ethanol in a chamber cooled to ⁇ 60 ° C., ethanol was injected into the pipe from a high-pressure hose to increase the internal pressure, and the pipe was ruptured. If the brittle fracture surface area ratio of the opening is less than 5%, it is listed in Table 6 as acceptable (indicated by ⁇ in Table 6) and rejected if not less than 5% (indicated by x in Table 6). .
  • test no. No. 22 was subjected to softening heat treatment soaking at 620 ° C. for 20 minutes before cold drawing.
  • Test No. 21 no. Except for No. 22, the cold drawing process could be finished in one time even without softening heat treatment after hot pipe making.
  • a high strength seamless steel pipe for an airbag system having excellent low temperature burst performance as an airbag accumulator component including a reduced diameter portion by performing induction quenching and tempering using steel of chemical composition according to the present invention. It is clear that can be manufactured inexpensively and with high efficiency.

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Abstract

La présente invention concerne un tube d'acier pour coussins de sécurité gonflable dont le coût de l'alliage est réduit et présentant une résistance à la traction supérieure ou égale à 1 000 MPa et une vTrs100 inférieure ou égale à -80ºC. Elle concerne également un processus de fabrication du tube d'acier selon lequel le nombre de traitements d'adoucissement/de recuit au cours de l'étape d'étirage à froid peut être réduit au minimum. Des propriétés de stabilité peuvent être obtenues y compris par l'intermédiaire d'un durcissement par trempe mis en œuvre par chauffage à haute fréquence à grande échelle. Le tube d'acier présente une composition d'acier contenant, en termes de % en masse, 0,05-0,20 % C, 0,10-0,50 % Si, 0,10-1,00 % Mn, jusqu'à 0,025 % P, jusqu'à 0,005 % S, 0,005-0,10 % Al, 0,0005-0,0050 % Ca, 0,005-0,050 % Nb, 0,005-0,050 % Ti, 0,01-0,50 % Cu, 0,01-0,50 % Ni, 0,01-0,50 % Cr, 0,0005-0,0050 % B, et 0,002-0,010 % N, le reste comprenant Fe et des impuretés accidentelles.
PCT/JP2010/059417 2010-06-03 2010-06-03 Tube d'acier pour coussin de sécurité gonflable et son processus de fabrication WO2011151908A1 (fr)

Priority Applications (10)

Application Number Priority Date Filing Date Title
EP10852513.0A EP2484793B1 (fr) 2010-06-03 2010-06-03 Tube d'acier pour coussin de sécurité gonflable et son processus de fabrication
CA2776984A CA2776984C (fr) 2010-06-03 2010-06-03 Tube d'acier pour coussin de securite gonflable et son processus de fabrication
KR1020127010714A KR101425738B1 (ko) 2010-06-03 2010-06-03 에어백용 강관과 그 제조 방법
MX2012005710A MX2012005710A (es) 2010-06-03 2010-06-03 Tubo de acero para bolsas de aire y un proceso para fabricar las mismas.
ES10852513T ES2726767T3 (es) 2010-06-03 2010-06-03 Tubo de acero para airbags y un proceso para la fabricación del mismo
PCT/JP2010/059417 WO2011151908A1 (fr) 2010-06-03 2010-06-03 Tube d'acier pour coussin de sécurité gonflable et son processus de fabrication
IN3019DEN2012 IN2012DN03019A (fr) 2010-06-03 2010-06-03
CN201080049152.0A CN102741438B (zh) 2010-06-03 2010-06-03 气囊用钢管及其制造方法
PL10852513T PL2484793T3 (pl) 2010-06-03 2010-06-03 Rura stalowa do poduszki powietrznej i sposób jej wytwarzania
US13/438,956 US9080223B2 (en) 2010-06-03 2012-04-04 Steel tube for airbags and a process for manufacturing same

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CN103147017A (zh) * 2013-03-21 2013-06-12 宝山钢铁股份有限公司 一种高强度优良低温韧性钢板及其制造方法
CN104073731B (zh) * 2013-03-27 2017-02-22 鞍钢股份有限公司 一种采用直接淬火工艺的超高强船板的生产方法
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JP6398575B2 (ja) * 2014-10-10 2018-10-03 新日鐵住金株式会社 靭性に優れた鋼板およびその製造方法
US20170094730A1 (en) * 2015-09-25 2017-03-30 John Justin MORTIMER Large billet electric induction pre-heating for a hot working process
SG11201900897RA (en) 2016-08-01 2019-02-27 Nippon Steel & Sumitomo Metal Corp Seamless steel pipe and method for producing same
CN107052717A (zh) * 2017-04-01 2017-08-18 浙江金固股份有限公司 轮辐制造方法
DE102018132816A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von thermo-mechanisch hergestellten profilierten Warmbanderzeugnissen
CN112593068A (zh) * 2020-12-03 2021-04-02 成都先进金属材料产业技术研究院有限公司 无缝钢管的连续等温退火方法
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EP2484793A4 (fr) 2016-01-13
EP2484793B1 (fr) 2019-03-13
CN102741438A (zh) 2012-10-17
US20120205016A1 (en) 2012-08-16
KR20120056890A (ko) 2012-06-04
EP2484793A1 (fr) 2012-08-08
IN2012DN03019A (fr) 2015-07-31
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PL2484793T3 (pl) 2019-09-30
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